CN109518084A - A kind of high heat conductance is containing Al, Nb nitriding hot die steel and preparation method thereof - Google Patents
A kind of high heat conductance is containing Al, Nb nitriding hot die steel and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
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Abstract
The invention discloses a kind of high heat conductance containing Al, Nb nitriding hot die steel and preparation method thereof.Hot die steel of the present invention is by percentage to the quality, include: C 0.40~0.50%, Si≤0.30%, Mn≤0.30%, Cr 2.00~3.50%, Mo 0.30~0.80%, V 0.60~0.80%, Al 0.50~0.90%, Nb 0.05~0.15%, P < 0.015%, S < 0.015%, Fe surplus.Base steel of the present invention adjusts C and Cr, Mo, V ratio in 4Cr5MoSiV1 steel alloy ingredient, adds Al, Nb, alloy content ratio 4Cr5MoSiV1 steel few 1.5~2.0%.Steel of the present invention is at low cost, toughness and 4Cr5MoSiV1 steel are suitable, has high heat conductance and nitriding, excellent wearability and resistance to tempering.
Description
Technical field
The invention belongs to metallurgical technology fields, and in particular to a kind of high heat conductance containing Al, Nb nitriding hot die steel and its
Preparation method.
Background technique
Benefit from automobile, electronics, plastic products demand increasingly increase, components thermoforming industry development is rapid.But by
In the particularity of thermoforming military service operating condition, it is desirable that die steel material has higher performance requirement, such as high heat conductance, high-temperature stable
Property, good high temperature friction and wear behavior etc..That the current hot die steel in China generallys use is standard GB/T/T1299-
3Cr2W8V, 4Cr5MoSiV1,4Cr5Mo2V steel in 2014, but less managed in drop stamping, hot extrusion industrial application effect
Think.Wherein 3Cr2W8V steel thermal conductivity and thermal fatigue resistance are poor, and modeling, toughness are low, are easy to happen early fracture, and chromium series hot
Mould steel 4Cr5MoSiV1 (H13) and 4Cr5Mo2V (DIEVAR) is generally no more than 600 DEG C, and high temperature wear longevity using temperature
Life is not high, influences shaped article surface quality.
For mold military service behavior, on the one hand in order to conduct the heats of components during thermoforming as early as possible, slow down mould
Has local damage softening, mold materials need higher thermal coefficient, elevated temperature strength and thermal stability；On the other hand, hot extrusion,
Die surface easily generates plucking during drop stamping is on active service, and mold materials need to have excellent wearability, or are easy to table
Surface treatment is to obtain abrasion resistance properties；There are certain shock loading during thermoforming simultaneously, excellent toughness can be protected effectively
Demonstrate,prove die life.
Therefore, at present under sustainable, Eco-power development model driving at home and abroad, from the angle of innovation, for
Market particular demands make full use of alloying element to stablize with comparison thermal conductivity and high tempering using economic alloyage process
Property effect, the present invention develops a kind of high heat conductance hot die steel containing Al, Nb nitriding, be China's independent development high-performance,
Long-life nitriding hot die steel has stepped essential step.
Summary of the invention
Goal of the invention: present invention aims in view of the deficiencies of the prior art, provide a kind of high heat conductance nitriding containing Al, Nb
Hot die steel and its method.The present invention is matched using a kind of chemical component of economy, is based on 4Cr5MoSiV1 steel alloy ingredient,
The ratio for adjusting C and carbide former Cr, Mo, V, obtains high thermal conductivity and resistance to tempering；It can be refined after addition Nb
Tissue and raising service temperature, addition Al rear surface nitriding are capable of forming AlN high abrasion hardening constituent, solve 4Cr5MoSiV1 steel
Anti- temper softening ability and the weak defect of wearability after surface carburization processing.Alloy content ratio 4Cr5MoSiV1 steel few 1.5~
2.0%, reduce production cost.Present invention accomplishes the current drop stamping in China, hot extruding die special-purpose steel kind lack status,
The ability for making China have independent development high-performance, long-life nitriding hot die steel.
Technical solution: the purpose of the invention is achieved by the following technical solution:
The present invention provides a kind of high heat conductance hot die steels containing Al, Nb nitriding, and the hot die steel is with quality hundred
Divide than meter, includes: C 0.40~0.50%, Si≤0.30%, Mn≤0.30%, Cr 2.00~3.50%, Mo 0.30~
0.80%, V 0.60~0.80%, Al 0.50~0.90%, Nb 0.05~0.15%, P < 0.015%, S < 0.015%,
Fe surplus.
The design principle of steel chemical composition of the present invention is as follows:
C: carbon can partially dissolve in steel plays the role of solution strengthening in matrix；Part forms alloy carbon with alloying element
Compound.The hardenability and harden ability of steel can be improved in the appropriate carbon content that improves；But when carbon content is excessively high, will lead to be formed it is excessive
Carbide and microstructure segregation influence the impact flexibility of steel.And when carbon element content is too low, it will cause and other alloying element knots
Conjunction forms that alloy carbide object amount is less, influences hardness, wearability and high-temperature behavior of steel etc..In carbon steel, the increase of carbon is reduced
Thermal conductivity, but its effect common with alloying element is considered in steel alloy to guarantee thermal conductivity and wear-resisting property.
Si: silicon is solution strengthening element.Silicone content is reduced, when making macrostructure's more uniformization, and can be reduced solidification
Constitutional supercooling on freezing interface increases plasticity and toughness.Element silicon can make point of steel martensite during tempering
Solution slows down, and the decomposition of martensite can be effectively hindered in drawing process.Silicon amount can aggravate the Decarburization Sensitivity of steel when excessively high, and
And the overaging speed for assembling carbide increases and is difficult to control.Silicon has negative impact to thermal conductivity in steel, contains
Amount, which increases, will be greatly reduced thermal conductivity.Therefore, the content of silicon should be controlled in reduced levels in steel of the present invention.
Mn: manganese has solution strengthening effect, to improve the intensity and hardness of ferrite and austenite, manganese element is weak carbon
Compound formation element.Manganese element can cause the content of retained austenite in steel to increase and stablize, and improve the toughness and heat resistanceheat resistant of steel
Fatigue behaviour.But manganese content is excessively high, promotes harmful element segregation to increase brittleness, weakens the resistance to corrosion of steel, reduction is led
Hot property, welding performance etc..Therefore the content of manganese maintains reduced levels in steel of the present invention.
Cr: chromium can be dissolved in ferrite, and can form carbide.Chromium, chromium member are added in hot die steel mostly
Element makes steel that Cr be precipitated during tempering7C3And Cr23C6Type carbide, this carbide are not only able to improve resisting back for steel
Fiery softening performance, and certain red hardness can be generated, improve the heat resistance of steel.But when tempering temperature is higher than 600 DEG C,
The carbide of chromium just aggregation roughening rapidly, so that the anti-tempering stabilization energy of steel is poor.And in terms of thermal conductivity, chromium content increases
It is big to the thermal conductivity damage effect of steel.Therefore chromium content is reduced compared with 4Cr5MoSiV1 steel in steel of the present invention.
Mo: molybdenum improves the harden ability and heat resistance of steel, reduces temper brittleness, increases temper resistance, refines crystal grain, improves
Red hardness.The addition of molybdenum element improves the stability of steel austenite and the harden ability of steel, and molybdenum element is that carbide forms member
Element combines with carbon during steel belt roof bolt and forms more stable M2C-type alloy carbide, in martensite lath
It is precipitated in sub boundary with parallel fine acicular position, keeps coherence with matrix, improve the high temperature hardness and wearability of steel.
V: vanadium is carbide, can be improved wearability in steel, while crystal grain can also be hindered to grow up, plays
Refine the effect of crystal grain.Solubility product of the vanadium carbide in austenite is higher, at high temperature as precipitation and caused by solidification group
The trend for knitting cracking is smaller.Suitable vanadium is added in steel and is conducive to austenite recrystallization, is easy to implement recrystallization control, very wide
Within the temperature range of, uniform recrystal grain can be obtained.Vanadium is added in martensite steel can increase the anti-temper softening of steel
Can, so that steel is kept martensite lath form in drawing process, or vanadium carbide is precipitated in drawing process, generates post-curing
Effect.The carbide stabilization and hardness with higher of vanadium, can be improved the wearability of mould steel.Heat of the addition of vanadium to steel
Conductance influence is smaller, weaker to the effect for the thermal conductivity for reducing steel.Consider effect of the vanadium in steel, considers addition in steel of the present invention
A certain amount of vanadium.
Nb: niobium is a kind of strong carbonitride-forming elements, can effectively prevent austenite when soaking from growing up, play refinement crystal grain
With the superheated susceptivity and temper brittleness for reducing steel.Meanwhile niobium can improving welding property and material at high temperature intensity.
Al: the affinity of aluminium and nitrogen, oxygen is very strong, and nitrogen agent is determined in deoxidation when as steel-making, plays refinement crystal grain, improves steel low
The effect of the lower toughness of temperature.Aluminium can improve the inoxidizability of steel when being added in steel as alloying element, in the surface shape of steel after nitriding
At the aln layer of one layer of firm thin and stiff Dispersed precipitate, improve wearability and fatigue strength of nitrided steel etc..
P: phosphorus is the harmful element in steel, improve the ductile-brittle transition temperature of steel, therefore strict control of the present invention P elements
Content.
S: sulphur is easy to be segregated in steel, deteriorates the quality of steel.Element sulphur is easy to make steel in hot-working in certain degree
During generate overheat and burn-off phenomenon.Therefore strict control of the present invention sulfur content.
Preferably, the hot die steel by percentage to the quality, includes: C 0.45%, Si 0.20%, Mn
0.24%, Cr 2.80%, Mo 0.72%, V 0.76%, Al 0.70%, Nb 0.09%, P 0.010%, S 0.013%,
Fe surplus.
In contrast hot die steel of the invention and universal hot die steel 4Cr5MoSiV1 steel, have higher lead
Heating rate, resistance to tempering, high temperature abrasion resistance and nitriding ability.Si, Cr content are reduced, increases the thermal conductivity of material, passes through Cr, Mo, V
With the balance of C, steel of the present invention is made to obtain high resistance to tempering and excellent harden ability, Nb element is added and effectively improves material military service temperature
Degree；Al element is added simultaneously can form AlN hardening constituent after surface carburization, and hardness is up to 1200HV or more, improve material surface
Wearability.
Preparation method the present invention also provides above-mentioned high heat conductance containing Al, Nb nitriding hot die steel, including following step
It is rapid:
(1) smelt: selection steel scrap, using electric furnace smelting method, by shifting to an earlier date slag making, steel is smelted and stayed to stokehold making foamed slag
Remaining slag operation obtains the low molten steel of P content；VD Fruit storage is carried out to molten steel after LF deoxidation, final vacuum is in 67Pa
Hereinafter, the dwell time is greater than 15min, then feeds silicon-calcium wire and carry out inclusion modification, then soft blow argon 5min or more, last argon gas is protected
Shield casting；
(2) electroslag remelting: using the steel ingot after pouring as consutrode, through 36~48min electroslag remelting at ESR ingot；Its
Between by wash heat removal of inclusions, to eliminate or mitigate various both macro and micro defects, ingredient and the tissue for improving steel ingot are equal
Even property；ESR ingot furnace cooling after remelting；
(3) forge: ESR ingot then carries out at 1080~1130 DEG C more through 1250 DEG C or more high temperature diffusion annealings before forging
It is processed to forging, forging ratio >=6, final forging temperature >=900 DEG C, furnace samming, furnace cooling annealing is sent after forging；
(4) spheroidizing: the forging material that step (3) is obtained carries out preparatory solution treatment, and temperature is 1090~1130 DEG C, and
Oil is cooled to 250 DEG C of surface temperature or less afterwards；Two-part spheroidizing is carried out after air-cooled samming, first stage annealing temperature is 830
~860 DEG C, secondary stage annealing temperature is 710~740 DEG C；
(5) it is heat-treated and is surface-treated: 1030~1100 DEG C of heat-treatment quenching temperature, after oil cooling or water cooling, 560~600
The processing of DEG C double tempering；500~550 DEG C of nitriding temperature of surface treatment, nitriding atmosphere is ammonia, 500~600Pa of furnace pressure.
Steel of the present invention can be widely applied to drop stamping, hot extrusion industry, have wide thermoforming application market.It is desirable
For gate-in mold system steel, gate-in mold system steel price is up to 200 yuan/kg, is 5~7 times of this steel cost price.Steel of the present invention has extremely
High industry added value.
Compared with prior art, the beneficial effects of the present invention are:
The present invention is based on 4Cr5MoSiV1 steel alloy ingredients, adjust the ratio of C and carbide former Cr, Mo, V, obtain
High thermal conductivity and resistance to tempering are obtained, addition Al element guarantees nitriding ability, and addition Nb element improves material at high temperature performance, develops
Having the hot die steel containing Al, Nb of high heat conductance and nitriding ability, resistance to tempering is 3~5 times of 4Cr5MoSiV1 steel,
Nitriding layer after surface carburization has a nitride layer, white layer, predominantly AlN hardening constituent, and hardness ratio H13 steel (CrN hardening constituent) is high by 120~
200HV, diffusion layer ratio H13 steel are 80~120 μm deep.
Detailed description of the invention
Fig. 1 is that high heat conductance of the present invention contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel is quenched and is tempered the punching of state room temperature
Hit impact flexibility comparison.
Fig. 2 is that high heat conductance of the present invention is compared containing Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel thermal conductivity.
Fig. 3 is that the high heat conductance of the embodiment of the present invention 1 contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel thermostabilization
Property (resistance to tempering) comparison.
Fig. 4 is that the high heat conductance of the embodiment of the present invention 2 contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel thermostabilization
Property (resistance to tempering) comparison.
Fig. 5 is that the high heat conductance of the embodiment of the present invention 3 contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel thermostabilization
Property (resistance to tempering) comparison.
Fig. 6 is that high heat conductance of the present invention contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel high temperature friction and wear
It can comparison.
Fig. 7 is that high heat conductance of the present invention contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel nitriding layer microhardness
Gradient comparison.
Fig. 8 is that high heat conductance of the present invention contains Al, Nb nitriding hot die steel and 4Cr5MoSiV1 steel nitriding layer comparison diagram.
Specific embodiment
Technical solution of the present invention is described in detail below by specific embodiments and the drawings, but protection of the invention
Range is not limited to the embodiment.
Embodiment 1
In the present embodiment, a kind of high heat conductance hot die steel containing Al, Nb nitriding includes by percentage to the quality:
C 0.45%, Si 0.20%, Mn 0.24%, Cr 2.80%, Mo 0.72%, V 0.76%, Al 0.70%,
Nb 0.09%, P 0.010%, S 0.013%, Fe surplus.
Preparation step is as follows:
(1) electric furnace smelting: using electric furnace smelting method, and by shifting to an earlier date slag making, stokehold making foamed slag is smelted and steel is stayed to stay slag
Operation obtains the low molten steel of P content；After LF deoxidation to molten steel carry out VD Fruit storage, final vacuum in 67Pa hereinafter,
Dwell time is greater than 15min, then feeds silicon-calcium wire and carries out inclusion modification, then soft blow argon 5min or more, last argon gas protection is poured
Casting；
(2) electroslag remelting: the steel ingot after pouring is placed in electroslag remelting device as consutrode, carries out electroslag weight
Molten, slugging voltage 50V, electric current 3800A, electric system voltage 55V, electric current 11500A, bind voltage 58V, current time 40min,
Electroslag remelting is at Ф 600mm ESR ingot；Therebetween by wash heat removal of inclusions, with furnace after 750 DEG C of heat preservation 8h after electroslag remelting
It is cooling；
(3) forge: diffusion annealing temperature is 1260 DEG C, annealing time 12h；By high temperature steel ingot in heat treatment descent of temperature
Multiway forging, forging ratio >=6, final forging temperature >=900 DEG C are carried out after to 1080 DEG C；In 860 DEG C of heat preservation 10h, furnace cooling after forging；
(4) spheroidizing: the forging material that step (3) is obtained carries out preparatory solution treatment, and solid solubility temperature is 1090 DEG C, heat preservation
Time is 12h；Then oil is cooled to 250 DEG C of surface temperature or less；Reheating sends heat-treatment furnace back to；First stage isothermal annealing temperature is
840 DEG C, annealing time 8h；Second stage isothermal annealing temperature is 740 DEG C, annealing time 16h；
(5) be heat-treated and be surface-treated: 1030 DEG C quenching, using oil be cooled to 250 DEG C or less it is air-cooled；Then carry out 580 DEG C
Tempering is tempered 2 times, every time tempering heat preservation 3h；550 DEG C of nitriding 12h, nitriding atmosphere are ammonia, flow 580mL/min, furnace
Interior air pressure 500Pa.
High heat conductance of the present invention contains Al, Nb nitriding hot die steel after above-mentioned smelting and hot-working and heat treatment, most
Finished product specification be 230mm × 600mm × 2400mm module, sampling be tested for the property and under equal conditions
4Cr5MoSiV1 steel compares:
A, which quenches, is tempered state hardness
Using GB/T 230.1-2018 metal material Rockwell hardness test standard, measuring steel quenching hardness of the present invention is
56HRC, tempering hardness 47HRC.
B, which quenches, is tempered state impact flexibility
Lateral impact sample is taken on blank, specimen size is 10mm × 10mm × 55mm, V2 type notch is opened, using North America
Die casting association NADCA#207 standard measures room temperature impact work value: steel grade 19.7J of the present invention, H13 steel 20.5J, and impact flexibility is horizontal
Quite, all reach the super Impact Toughness of Steel requirement of NADCA#207 standard, test result is as shown in Fig. 1.
C thermal conductivity
Thermal diffusion coefficient or thermal coefficient testing standard are measured using GB/T 22588-2008 flicker method, measure the present invention
Thermal coefficient remains 32.0W/mK at 100~600 DEG C of steel, and 700 DEG C of thermal coefficients drop to 29.8W/mK.
Thermal coefficient is maintained at 30.0W/mK at 100~500 DEG C of 4Cr5MoSiV1 steel, and extraordinary wave occur in 600 DEG C or more thermal coefficients
It is dynamic.Steel of the present invention has wide steady heat conduction rate temperature range and high thermal coefficient, test result compared with 4Cr5MoSiV1 steel
As shown in Fig. 2.
D thermal stability (resistance to tempering)
Steel of the present invention, which is quenched, is tempered state at 620 DEG C, 650 DEG C with the progress stability contrast test of 4Cr5MoSiV1 steel, uses
GB/T 230.1-2018 metal material Rockwell hardness test standard carries out hardness test, as a result as shown in Fig. 3.Two kinds of tests
Steel initial hardness is 47HRC, and with the extension of soaking time, steel of the present invention and 4Cr5MoSiV1 steel hardness difference increase, and is surveyed
Test result is as shown in Fig. 3.After 620 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 38.8HRC, 4Cr5MoSiV1 steel 30.1HRC；
After 650 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 30.6HRC, 4Cr5MoSiV1 steel 25.6HRC.650 DEG C of steel tempering of the present invention are hard
The time that degree is maintained at 35HRC or more is 12h, and 4Cr5MoSiV1 steel is 3h, and the anti-temper softening ability of steel of the present invention is H13 steel
4 times.
E high temperature friction and wear behavior
It tests and grinds through Contour GT-K type optical profilometer after being tested using UMT-3 high temperature friction and wear testing machine
Loss rate, 100~700 DEG C of wear rates of steel of the present invention and 4Cr5MoSiV1 steel are increased with test temperature and are gradually increased, as a result as attached
Shown in Fig. 6.Two kinds of steel, 100~500 DEG C of wear rates are suitable, and value is lower than 2.5 × 10-8mm3/ Nm, and test temperature is higher than 600
DEG C, steel of the present invention is less compared with the rising of 4Cr5MoSiV1 steel wear rate, and 700 DEG C of wear rates of steel of the present invention are 4.68 × 10-8mm3/N·
M, 4Cr5MoSiV1 steel are 12.88 × 10-8mm3/ Nm, steel high temperature friction and wear behavior of the present invention is H13 steel at a temperature of this
2.8 again.
F nitriding layer microhardness gradient
Using GB/T 4340.1-2009 Vickers Hardness Test of Metallic Materials standard, after the specimen cross section grinding and polishing after nitriding
Vickers hardness test is carried out from surface layer to matrix, as a result as shown in Fig. 7.The surface carburization layer hardness of steel of the present invention is
1090HV, 4Cr5MoSiV1 steel are 888HV, and steel nitriding layer hardness of the present invention is higher by 4Cr5MoSiV1 steel under identical depth of penetration
140~200HV.Steel nitriding layer hardness 600HV or more of the present invention with a thickness of 200 μm, 4Cr5MoSiV1 steel is 125 μm, this hair
The effective nitrided case depth of bright steel is 1.6 times of 4Cr5MoSiV1 steel.
G nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 8.The present invention
There are nitride layer, white layer (i.e. AlN compound layers) for steel, and the nitride layer, white layer (i.e. CrN compound layer) of 4Cr5MoSiV1 steel is hardly visible；
And the nitrided case depth ratio 4Cr5MoSiV1 steel of steel of the present invention is higher by 80~120 μm.
Embodiment 2
In this example, a kind of high heat conductance hot die steel containing Al, Nb nitriding includes by percentage to the quality:
C 0.50%, Si 0.15%, Mn 0.28%, Cr 2.10%, Mo 0.32%, V 0.63%, Al 0.50%,
Nb 0.05%, P 0.010%, S 0.010%, Fe surplus.
Preparation step is as follows:
(1) electric furnace smelting: using electric furnace smelting method, and by shifting to an earlier date slag making, stokehold making foamed slag is smelted and steel is stayed to stay slag
Operation obtains the low molten steel of P content；After LF deoxidation to molten steel carry out VD Fruit storage, final vacuum in 67Pa hereinafter,
Dwell time is greater than 15min, then feeds silicon-calcium wire and carries out inclusion modification, then soft blow argon 5min or more, last argon gas protection is poured
Casting；
(2) electroslag remelting: the steel ingot after pouring is placed in electroslag remelting device as consutrode, carries out electroslag weight
Molten, slugging voltage 50V, electric current 4500A, electric system voltage 55V, electric current 12500A, bind voltage 58V, current time 36min,
Electroslag remelting is at Ф 600mm ESR ingot；Therebetween by wash heat removal of inclusions, with furnace after 850 DEG C of heat preservation 8h after electroslag remelting
It is cooling；
(3) forge: diffusion annealing temperature is 1250 DEG C, annealing time 10h；By high temperature steel ingot in heat treatment descent of temperature
Multiway forging, forging ratio >=6, final forging temperature >=900 DEG C are carried out after to 1100 DEG C；In 890 DEG C of heat preservation 8h, furnace cooling after forging；
(4) spheroidizing: the forging material that step (3) is obtained carries out preparatory solution treatment, and solid solubility temperature is 1100 DEG C, heat preservation
Time is 10h；Then water cooling is to 250 DEG C of surface temperature or less；Reheating sends heat-treatment furnace back to, and first stage isothermal annealing temperature is
830 DEG C, annealing time 8h；Second stage isothermal annealing temperature is 710 DEG C, annealing time 12h；
(5) it is heat-treated and is surface-treated: 1050 DEG C of quenchings, it is air-cooled using being water-cooled to 250 DEG C or less；Then carry out 560
DEG C tempering is tempered 2 times, every time tempering heat preservation 4h；520 DEG C of nitriding 12h, nitriding atmosphere are ammonia, flow 620mL/min,
Air pressure 600Pa in furnace.
High heat conductance of the present invention contains Al, Nb nitriding hot die steel after above-mentioned smelting and hot-working and heat treatment, most
Finished product specification be 280mm × 600mm × 2200mm module, sampling be tested for the property and under equal conditions
4Cr5MoSiV1 steel compares:
A, which quenches, is tempered state hardness
Using GB/T 230.1-2018 metal material Rockwell hardness test standard, measuring steel quenching hardness of the present invention is
55HRC, tempering hardness 48HRC.
B, which quenches, is tempered state impact flexibility
Lateral impact sample is taken on blank, specimen size is 10mm × 10mm × 55mm, V2 type notch is opened, using North America
Die casting association NADCA#207 standard measures room temperature impact work value.Room temperature impact work value: steel grade 21.9J of the present invention, H13 steel
20.5J, impact flexibility are on close level, and the super Impact Toughness of Steel requirement of NADCA#207 standard, test result such as attached drawing 1 are all reached
It is shown.
C thermal conductivity
Thermal diffusion coefficient or thermal coefficient testing standard, steel 100 of the present invention are measured using GB/T 22588-2008 flicker method
Thermal coefficient gradually slowly declines at~600 DEG C, is worth for 32.0~34.0W/mK, and 700 DEG C of thermal coefficients decline suddenly.
Thermal coefficient is maintained at 30.0W/mK at 100~500 DEG C of 4Cr5MoSiV1 steel, and extraordinary wave occur in 600 DEG C or more thermal coefficients
It is dynamic.Steel of the present invention has wide steady heat conduction rate temperature range and high thermal coefficient, test result compared with 4Cr5MoSiV1 steel
As shown in Fig. 2.
D thermal stability (resistance to tempering)
Steel of the present invention, which is quenched, is tempered state at 620 DEG C, 650 DEG C with the progress stability contrast test of 4Cr5MoSiV1 steel, uses
GB/T 230.1-2018 metal material Rockwell hardness test standard carries out hardness test, as a result as shown in Fig. 4.Two kinds of tests
Steel initial hardness is 47HRC, and with the extension of soaking time, steel of the present invention and 4Cr5MoSiV1 steel hardness difference increase, and is surveyed
Test result is as shown in Fig. 4.After 620 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 37.0HRC, 4Cr5MoSiV1 steel 30.1HRC；
After 650 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 30.4HRC, 4Cr5MoSiV1 steel 25.6HRC.650 DEG C of steel tempering of the present invention are hard
The time that degree is maintained at 35HRC or more is 10h, and 4Cr5MoSiV1 steel is 3h, and the anti-temper softening ability of steel of the present invention is H13 steel
3.3 times.
E high temperature friction and wear behavior
It tests and grinds through Contour GT-K type optical profilometer after being tested using UMT-3 high temperature friction and wear testing machine
Loss rate, 100~700 DEG C of wear rates of steel of the present invention and 4Cr5MoSiV1 steel are increased with test temperature and are gradually increased, as a result as attached
Shown in Fig. 6.Steel of the present invention is lower compared with 100~400 DEG C of wear rates of 4Cr5MoSiV1 steel, and 400 DEG C of wear rates of steel of the present invention are 1.40
×10-8mm3/ Nm, 4Cr5MoSiV1 steel are 2.58 × 10-8mm3/N·m；And test temperature be higher than 500 DEG C, steel of the present invention with
4Cr5MoSiV1 steel wear rate is suitable, therefore 100~700 DEG C of high temperature friction and wear behaviors of steel of the present invention are more preferable compared with H13 steel.
F nitriding layer microhardness gradient
Using GB/T 4340.1-2009 Vickers Hardness Test of Metallic Materials standard, after the specimen cross section grinding and polishing after nitriding
Vickers hardness test is carried out from surface layer to matrix, as a result as shown in Fig. 7.The surface carburization layer hardness of steel of the present invention is
1134HV, 4Cr5MoSiV1 steel are 888HV, and steel nitriding layer hardness of the present invention is higher by 4Cr5MoSiV1 steel under identical depth of penetration
140~200HV.Steel nitriding layer hardness 600HV or more of the present invention with a thickness of 200 μm, 4Cr5MoSiV1 steel is 125 μm, this hair
The effective nitrided case depth of bright steel is 1.6 times of 4Cr5MoSiV1 steel.
G nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 8.The present invention
There are nitride layer, white layer (i.e. AlN compound layers) for steel, and the nitride layer, white layer (i.e. CrN compound layer) of 4Cr5MoSiV1 steel is hardly visible；
And the nitrided case depth ratio 4Cr5MoSiV1 steel of steel of the present invention is higher by 80~120 μm.
Embodiment 3
In this example, a kind of high heat conductance hot die steel containing Al, Nb nitriding includes by percentage to the quality:
C 0.40%, Si 0.17%, Mn 0.23%, Cr 3.50%, Mo 0.80%, V 0.79%, Al 0.90%,
Nb 0.15%, P 0.010%, S 0.010%, Fe surplus.
Preparation step is as follows:
(1) electric furnace smelting: using electric furnace smelting method, and by shifting to an earlier date slag making, stokehold making foamed slag is smelted and steel is stayed to stay slag
Operation obtains the low molten steel of P content；After LF deoxidation to molten steel carry out VD Fruit storage, final vacuum in 67Pa hereinafter,
Dwell time is greater than 15min, then feeds silicon-calcium wire and carries out inclusion modification, then soft blow argon 5min or more, last argon gas protection is poured
Casting；
(2) electroslag remelting: the steel ingot after pouring is placed in electroslag remelting device as consutrode, carries out electroslag weight
Molten, slugging voltage 60V, electric current 2500A, electric system voltage 60V, electric current 11500A, bind voltage 62V, current time 48min,
Electroslag remelting is at Ф 600mm ESR ingot；Therebetween by wash heat removal of inclusions, with furnace after 800 DEG C of heat preservation 10h after electroslag remelting
It is cooling；
(3) forge: diffusion annealing temperature is 1280 DEG C, annealing time 15h；By high temperature steel ingot in heat treatment descent of temperature
Multiway forging, forging ratio >=6, final forging temperature >=900 DEG C are carried out after to 1130 DEG C；In 840 DEG C of heat preservation 10h, furnace cooling after forging；
(4) spheroidizing: the forging material that step (3) is obtained carries out preparatory solution treatment, and solid solution temperature is 1130 DEG C,
Soaking time is 9h；Then oil is cooled to 250 DEG C or less；Reheating sends heat-treatment furnace back to, and first stage isothermal annealing temperature is 860
DEG C, annealing time 6h；Second stage isothermal annealing temperature is 720 DEG C, annealing time 14h；
(5) be heat-treated and be surface-treated: 1100 DEG C quenching, using oil be cooled to 250 DEG C or less it is air-cooled；Then carry out 600
DEG C tempering is tempered 2 times, every time tempering heat preservation 2h；500 DEG C of nitriding 16h, nitriding atmosphere are ammonia, flow 580mL/min,
Air pressure 550Pa in furnace.
High heat conductance of the present invention contains Al, Nb nitriding hot die steel after above-mentioned smelting and hot-working and heat treatment, most
Finished product specification be 280mm × 600mm × 2200mm module, sampling be tested for the property and under equal conditions
4Cr5MoSiV1 steel compares:
A, which quenches, is tempered state hardness
Using GB/T 230.1-2018 metal material Rockwell hardness test standard, measuring steel quenching hardness of the present invention is
55HRC, tempering hardness 48HRC.
B, which quenches, is tempered state impact flexibility
Lateral impact sample is taken on blank, specimen size is 10mm × 10mm × 55mm, V2 type notch is opened, using North America
Die casting association NADCA#207 standard measures room temperature impact work value.Room temperature impact work value: steel grade 19.0J of the present invention, H13 steel
20.5J, impact flexibility are on close level, and the super Impact Toughness of Steel requirement of NADCA#207 standard, test result such as attached drawing 1 are all reached
It is shown.
C thermal conductivity
Thermal diffusion coefficient or thermal coefficient testing standard, steel 100 of the present invention are measured using GB/T 22588-2008 flicker method
Thermal coefficient remains 31.0W/mK at~700 DEG C, except 600 DEG C of thermal coefficients rise to 33.8W/mK.4Cr5MoSiV1
Thermal coefficient is maintained at 30.0W/mK at 100~500 DEG C of steel, and unusual fluctuations occur in 600 DEG C or more thermal coefficients.Steel of the present invention
There is wide steady heat conduction rate temperature range and high thermal coefficient compared with 4Cr5MoSiV1 steel, test result is as shown in Fig. 2.
D thermal stability (resistance to tempering)
Steel of the present invention, which is quenched, is tempered state at 620 DEG C, 650 DEG C with the progress stability contrast test of 4Cr5MoSiV1 steel, uses
GB/T 230.1-2018 metal material Rockwell hardness test standard carries out hardness test, as a result as shown in Fig. 5.Two kinds of tests
Steel initial hardness is 47HRC, and with the extension of soaking time, steel of the present invention and 4Cr5MoSiV1 steel hardness difference increase, and is surveyed
Test result is as shown in Fig. 5.After 620 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 39.5HRC, 4Cr5MoSiV1 steel 30.1HRC；
After 650 DEG C of heat preservations for 24 hours, steel hardness of the present invention is 31.7HRC, 4Cr5MoSiV1 steel 25.6HRC.650 DEG C of steel tempering of the present invention are hard
The time that degree is maintained at 35HRC or more is 14h, and 4Cr5MoSiV1 steel is 3h, and the anti-temper softening ability of steel of the present invention is H13 steel
4.7 times.
E high temperature friction and wear behavior
It tests and grinds through Contour GT-K type optical profilometer after being tested using UMT-3 high temperature friction and wear testing machine
Loss rate, 100~700 DEG C of wear rates of steel of the present invention and 4Cr5MoSiV1 steel are increased with test temperature and are gradually increased, as a result as attached
Shown in Fig. 6.Two kinds of steel, 100~500 DEG C of wear rates are suitable, and value is lower than 2.0 × 10-8mm3/ Nm, and test temperature is higher than 600
DEG C, steel of the present invention is less compared with the rising of 4Cr5MoSiV1 steel wear rate, and 700 DEG C of wear rates of steel of the present invention are 5.49 × 10-8mm3/N·
M, 4Cr5MoSiV1 steel are 12.88 × 10-8mm3/ Nm, high temperature friction and wear behavior of steel of the present invention is H13 steel at a temperature of this
2.3 times.
F nitriding layer microhardness gradient
Using GB/T 4340.1-2009 Vickers Hardness Test of Metallic Materials standard, after the specimen cross section grinding and polishing after nitriding
Vickers hardness test is carried out from surface layer to matrix, as a result as shown in Fig. 7.The surface carburization layer hardness of steel of the present invention is 994HV,
4Cr5MoSiV1 steel is 888HV, under identical depth of penetration steel nitriding layer hardness of the present invention be higher by 4Cr5MoSiV1 steel 120~
170HV.Steel nitriding layer hardness 600HV or more of the present invention with a thickness of 180 μm, 4Cr5MoSiV1 steel is 125 μm, steel of the present invention
Effective nitrided case depth is 1.4 times of 4Cr5MoSiV1 steel.
G nitriding layer tissue
To the specimen cross section after nitriding according to metallographic preparation method, observed after grinding and polishing corrosion, as shown in Fig. 8.The present invention
There are nitride layer, white layer (i.e. AlN compound layers) for steel, and the nitride layer, white layer (i.e. CrN compound layer) of 4Cr5MoSiV1 steel is hardly visible；
And the nitrided case depth ratio 4Cr5MoSiV1 steel of steel of the present invention is higher by 80~120 μm.
It is therefore seen that hot die steel of the invention compared with 4Cr5MoSiV1 steel have wide steady heat conduction rate temperature range with
And high thermal coefficient, resistance to tempering are 3~5 times of 4Cr5MoSiV1 steel, the nitriding layer after surface carburization has nitride layer, white layer, main
It to be AlN hardening constituent, hardness ratio H13 steel (CrN hardening constituent) high 120~200HV, diffusion layer ratio H13 steel is 80~120 μm deep.
As described above, must not be explained although the present invention has been indicated and described referring to specific preferred embodiment
For the limitation to invention itself.It without prejudice to the spirit and scope of the invention as defined in the appended claims, can be right
Various changes can be made in the form and details for it.
Claims (3)
1. a kind of high heat conductance hot die steel containing Al, Nb nitriding, which is characterized in that the hot die steel is with mass percent
Meter includes: C 0.40~0.50%, Si≤0.30%, Mn≤0.30%, Cr 2.00~3.50%, Mo 0.30~0.80%,
V 0.60~0.80%, Al 0.50~0.90%, Nb 0.05~0.15%, P < 0.015%, S < 0.015%, Fe surplus.
2. high heat conductance according to claim 1 hot die steel containing Al, Nb nitriding, which is characterized in that the Forming Die
Have steel by percentage to the quality, includes: C 0.45%, Si 0.20%, Mn 0.24%, Cr 2.80%, Mo 0.72%, V
0.76%, Al 0.70%, Nb 0.09%, P 0.010%, S 0.013%, Fe surplus.
3. preparation method of the high heat conductance according to claim 1 containing Al, Nb nitriding hot die steel, which is characterized in that
The following steps are included:
(1) smelt: selection steel scrap, using electric furnace smelting method, by shifting to an earlier date slag making, stokehold making foamed slag is smelted and steel is stayed to stay slag
Operation obtains the low molten steel of P content；After LF deoxidation to molten steel carry out VD Fruit storage, final vacuum in 67Pa hereinafter,
Dwell time is greater than 15min, then feeds silicon-calcium wire and carries out inclusion modification, then soft blow argon 5min or more, last argon gas protection is poured
Casting；
(2) electroslag remelting: using the steel ingot after pouring as consutrode, through 36~48min electroslag remelting at ESR ingot；Lead to therebetween
Wash heat removal of inclusions is crossed, ESR ingot furnace cooling after remelting；
(3) forge: ESR ingot then carries out multidirectional forging through 1250 DEG C or more high temperature diffusion annealings at 1080~1130 DEG C before forging
Processing, forging ratio >=6 are made, furnace samming, furnace cooling annealing are sent in final forging temperature >=900 DEG C after forging；
(4) spheroidizing: the forging material that step (3) is obtained carries out preparatory solution treatment, and temperature is 1090~1130 DEG C, then oily
It is cooled to 250 DEG C of surface temperature or less；Two-part spheroidizing is carried out after air-cooled samming, first stage annealing temperature is 830~860
DEG C, secondary stage annealing temperature is 710~740 DEG C；
(5) it is heat-treated and is surface-treated: 1030~1100 DEG C of heat-treatment quenching temperature, after oil cooling or water cooling, 560~600 DEG C two
Secondary tempering；500~550 DEG C of nitriding temperature of surface treatment, nitriding atmosphere is ammonia, 500~600Pa of furnace pressure.
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| CN110016619A (en) * | 2019-05-28 | 2019-07-16 | 营口市特殊钢锻造有限责任公司 | A kind of mining High Strength Wear-Resistance Material and preparation method thereof |
| CN110835670A (en) * | 2019-09-30 | 2020-02-25 | 鞍钢股份有限公司 | High-wear-resistance high-hardness easy-cutting high-end mirror surface plastic die steel and preparation method thereof |
| CN111057933A (en) * | 2019-12-17 | 2020-04-24 | 安徽旭通网络科技有限公司 | Manufacturing process of hot-work die steel for high-performance die-casting die |
| CN112024798A (en) * | 2020-08-25 | 2020-12-04 | 无锡继平锻造有限公司 | Forging and machining process of rear pipe forging for special ship |
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Application publication date: 20190326 |